JP2005121535A - Method for simulating rubber material - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a method for analyzing the deformed state of a rubber material precisely. <P>SOLUTION: The method for simulating the rubber material is used to simulate the deformation of the rubber material in which a filler is blended. The method includes a step for setting a rubber material model in which the rubber material is modelled by an element capable of a numeric analysis. The rubber material model 2 includes a matrix model 3 in which a rubber matrix is modelled; a filler model 4 in which the filler is modelled; and an interface model 5 for forming the interface between the matrix model 3 and the filler model 4. <P>COPYRIGHT: (C)2005,JPO&NCIPI

Description

  The present invention relates to a rubber material simulation method useful for accurately analyzing a deformation state of a rubber material.

  Rubber materials are used in tires, sporting goods, and other various industrial products. The rubber material is greatly deformed when subjected to a load, and can be restored to its original state when the load is completely removed. The rubber material has non-linearity in which stress and strain are not proportional to each other during deformation, and the stress-strain curve path is different between when a load is applied and when the load is unloaded. In order to reduce the labor and cost of prototyping, a process of deforming a rubber material is simulated in advance using a computer. Conventionally, as a rubber material simulation method, the following Patent Document 1, Non-Patent Document 1, and the like are known.

JP 2002-365205 A Ellen M. Arruda and Marry C. Boyce `` A THREE-DIMENSIONAL CONSTITUTIVE MODEL FOR THE LARGE STRECH BEHAVIOR OF RUBBER ELASTIC MATERIALSS '' Journal of the Mechanics and Physics of Solids Volume 41, Issue 2, Pages 389-412 (February 1993)

  Patent Document 1 focuses on the fact that a rubber material (viscoelastic material) exhibits different longitudinal elastic modulus depending on the strain rate. Specifically, the strain, strain rate, stress, etc. generated in the viscoelastic material are measured in advance under the measurement conditions assuming the actual usage state of the viscoelastic material, and the correspondence relationship between the longitudinal elastic modulus and the strain or strain rate is determined. A derivation step is performed. A predetermined strain rate is given to the product model of the viscoelastic material to be analyzed, and a deformation simulation is performed by appropriately calculating the longitudinal elastic modulus from the above correspondence. Since the method of patent document 1 includes the trial that the longitudinal elastic modulus of a viscoelastic material changes according to a strain rate, it can evaluate in the point which can take in hysteresis loss in simulation.

  Further, Non-Patent Document 1 proposed by Arruda et al. Describes that a rubber material is modeled and calculated up to a polymer level by using a molecular chain network theory. Here, the molecular chain network theory will be briefly described.

  In the molecular chain network theory, as shown in FIGS. 16A and 16B, the rubber material a as a continuum has a microscopic structure in which randomly oriented molecular chains c are connected at junctions b. The premise is that it has a mesh structure. The junction point b is, for example, a chemical bond between molecules, and includes a crosslinking point.

  One molecular chain c is composed of a plurality of segments d as shown in FIG. One segment d is a repeating minimum structural unit in the molecular chain network theory. One segment d is chemically equivalent to a plurality of monomers f in which carbon atoms are connected by covalent bonds, as shown in FIG. Since the individual carbon atoms can freely rotate around the bond axis between the atoms, the segment d can take various forms such as winding as a whole.

  In the molecular chain network theory, it is assumed that the average position of the junction b does not change for a long time with respect to the atomic fluctuation period, and the perturbation around the junction b is ignored. It is further assumed that the end-to-end vector of the molecular chain c having two junctions b, b at both ends co-deforms with the rubber material continuum in which it is embedded.

  Aruuda et al. Have proposed a further eight-chain model based on molecular chain network theory. As shown in FIG. 4A, the viscoelastic material can be considered macroscopically as a cubic network structure h in which minute 8-chain models g are assembled. As shown in an enlarged view in FIG. 4B, one 8-chain model g is composed of eight junction points provided at each vertex from one junction point b1 in which the molecular chain c is defined at the center of the cube. It is assumed that it extends to b2.

The rubber material is treated as a superelastic body (a material that hardly changes in volume and returns to its original shape after unloading) in the simulation. A superelastic body is defined as a substance having a strain energy function W that generates a conjugate kirchhoff stress S _ij by being differentiated by a Green strain component E _ij as shown in the following formula (1). The In other words, the strain energy function presupposes the presence of potential energy stored when the rubber material is deformed. Therefore, the stress and strain relationship can be obtained from the differential gradient of the strain energy function W.

Aruuda et al., Based on non-Gaussian chain theory, thought that the entropy change suddenly increases (the molecular chain stretches and orients) as the deformation of the rubber material increases, and the strain energy function W of the rubber elastic body of equation (2) showed that. Then, by substituting this strain energy function W into the above equation, the relationship between the stress and strain of the rubber material can be extracted.

  By performing a deformation simulation of a viscoelastic material using the relationship between stress and strain of Aruuda et al., For example, as shown in FIG. 17, in a uniaxial tensile deformation simulation, a relationship between nonlinear stress and strain is obtained. Can do. This result shows a good correlation with the actually measured value when the load is deformed.

  A rubber material used as an industrial product usually contains a filler (filler) such as carbon black. When a deformation simulation of a rubber material containing such a filler is performed, how to handle the interface between the filler and the matrix rubber is an important problem. As a result of various studies, various phenomena have occurred at the interface, and it has recently been found that a slip or friction phenomenon between the rubber matrix and the filler at the interface causes a relatively large energy loss. Therefore, in order to simulate a rubber material with high accuracy, it is important to incorporate such an interface as a model.

  However, Patent Document 1 does not consider the interface between the rubber matrix and the filler. The same applies to Non-Patent Document 2.

  The present invention has been devised in view of the above problems. A rubber material model is a matrix model in which a rubber matrix is modeled, a filler model in which a filler is modeled, the matrix model, and the filler model. The purpose is to provide a rubber material simulation method capable of accurately deforming and simulating rubber materials by giving unique characteristics to the interface based on the interface model that forms the interface between Yes.

  The invention according to claim 1 of the present invention is a rubber material simulation method for simulating deformation of a rubber material mixed with a filler, and a rubber material model in which the rubber material is modeled by an element capable of numerical analysis. A step of setting a condition in the rubber material model and performing a deformation calculation, and obtaining a necessary physical quantity from the deformation calculation, and the rubber material model models a rubber matrix. The method of simulating a rubber material, comprising: a matrix model that is formed, a filler model that models a filler, and an interface model that forms an interface between the matrix model and the filler model.

  The invention according to claim 2 is the rubber material simulation method according to claim 1, wherein the interface model defines viscoelastic characteristics different from the matrix model.

  The invention according to claim 3 is the rubber material simulation method according to claim 1, characterized in that the interface model defines softer viscoelastic properties than the matrix model.

  The invention according to claim 4 is the rubber material simulation method according to claim 1, wherein the interface model defines a harder viscoelastic property than the matrix model.

  The invention according to claim 5 is characterized in that the interface model defines a viscoelastic property having a hysteresis loss larger than that of the matrix model, and the simulation of the rubber material according to any one of claims 1 to 4 Is the method.

  In the rubber material simulation method of the present invention, a rubber material model to be analyzed includes a matrix model in which a rubber matrix is modeled, a filler model in which a filler is modeled, and the matrix model and the filler model. And an interface model for forming an interface. Therefore, the influence of the interface can be taken into the calculation result, and a highly accurate simulation according to the characteristics of the actual viscoelastic material is possible.

Hereinafter, an embodiment of the present invention will be described with reference to the drawings.
FIG. 1 shows a computer apparatus 1 for carrying out the simulation method of the present invention. The computer device 1 includes a main body 1a, a keyboard 1b as an input means, a mouse 1c, and a display device 1d as an output means. Although not shown, the main body 1a is provided with a processing unit (CPU), a ROM, a working memory, a mass storage device such as a magnetic disk, and CD-ROM and flexible disk drives 1a1 and 1a2. The mass storage device stores a processing procedure (program) for executing a simulation method of the present invention, which will be described later. The computer device 1 is preferably EWS or the like.

  FIG. 2 shows an example of the processing procedure of the simulation method. In the present embodiment, first, a rubber material model in which a filler is blended is set (step S1). In FIG. 3, an example of the rubber material model 2 as a microscopic structure is visualized.

  The rubber material model 2 is obtained by replacing a minute region of a rubber material to be analyzed (whether or not actually exist) with a finite number of small elements 2a, 2b, 2c. Each element 2a, 2b, 2c... Is defined so as to be capable of numerical analysis. The possibility of numerical analysis means that deformation calculation for each element or the entire system can be performed by a numerical analysis method such as a finite element method, a finite volume method, a difference method, or a boundary element method. Specifically, for each element 2a, 2b, 2c..., A node coordinate value, an element shape, a material characteristic, etc. in the coordinate system are defined. For each of the elements 2a, 2b, 2c, etc., for example, a triangular or quadrilateral element as a two-dimensional plane, and a tetrahedral element, for example, is preferably used as a three-dimensional element. Thus, the rubber material model 2 can constitute numerical data that can be handled by the computer device 1.

  The rubber material model 2 of this embodiment is analyzed in a plane strain state in a deformation simulation described later. Therefore, there is no distortion in the Z direction. The length of one side of the rubber material model 2 is, for example, 300 nm × 300 nm in both vertical and horizontal directions.

  The rubber material model 2 of this embodiment includes a matrix model 3 (the darkest part) in which a rubber matrix portion is modeled, and a filler (filler) that is distributed and arranged in the matrix model 3. And a filler model 4 (white portion) and an interface model 5 (slightly black portion) that is interposed between the matrix model 3 and the filler model 4 and forms an interface between the two. .

The matrix model 3 constitutes a main part of the rubber material model 2 and is expressed using, for example, triangular or quadrilateral elements. For each element constituting the matrix model 3, the relationship between stress and strain of the following formula (3) is defined as material characteristics. Therefore, the matrix model 3 can obtain the relationship between stress and strain for each element.

Here, the derivation process of Equation (3) will be described. The rubber material has a small volume change due to deformation, and can be ignored. Therefore, the non-compressible viscoelastic material, a non-compression condition can be the density is constant, Kirchhoff stress S _ij can be expressed by Equation (4). E _ij is a component of Green strain, p is hydrostatic pressure (determined by boundary conditions), X _i is a position of an arbitrary object point P in a state C 0 where stress and strain are 0, and x _j is a deformed state C Is the position of the object point P.

The Cauchy stress component σ _ij and the kirchhoff stress component S _mn have the relationship of the following formula (5). Therefore, Expression (6) can be obtained from Expression (4).

Here, when the volume is constant, J in Equation (5) indicating the volume change rate of the object can be regarded as 1. Further, since the strain energy function of Equation (2) is a function of only the first-order invariant I ₁ of the strain of the left Cauchy-Green deformation tensor A _ij , Equations (6) to (7) are obtained.

Further, by using the following relational expressions (8 to 10), the speed format display of Expression (7) becomes Expression (11).

  And, there is no essential difference even if the Jaumann velocity of the Cauchy stress shown in Equation (11) is replaced with the Jaumann velocity of the kirchhoff stress, and the deformation rate tensor D is replaced with the strain rate tensor. Thus, the speed format display of the constitutive formula of the incompressible viscoelastic material can be expressed by the formula (3).

  However, when only this formula (3) is used, energy loss, which is one of the characteristics of the rubber material, cannot be taken into account, as in Non-Patent Document 1 by Aruuda et al. That is, when a simulation of unloading from the state Q in FIG. 17 is performed, strain recovery is performed through substantially the same path as the curve. With this, a hysteresis loop is not formed and energy loss cannot be calculated.

  The inventors tried various experiments based on the model of Aruuda et al. First, it is considered that the rubber material is allowed to have a large strain that can reach several hundreds of percent by extending the long molecular chain c intertwined in a complicated manner as described above. Therefore, the inventors unraveled the intertwined portions of the molecular chains c of the viscoelastic material in the deformation process under load (reduction of the number of joint points b), or further entanglement (unbonding) by unloading the load. An assumption was made that an increase in the number of points b) may occur. In other words, this assumption means that the average number of segments N per molecular chain in the equation (1) is a variable parameter during loading or unloading deformation. The inventors verified this assumption and found that the hysteresis of the viscoelastic material can be expressed.

  As described above, in the rubber material model 2 of the present embodiment, the average number of segments N per molecular chain is defined as a parameter different in load deformation and unload deformation in the formula (3). . Thereby, each element of the matrix model 3 can capture an energy loss in calculation. Here, at the time of load deformation is a deformation in which the strain of the model increases during a very short time, and conversely, at the time of unloading deformation means a deformation in which the strain decreases.

  4A shows a macroscopic three-dimensional network structure h of a viscoelastic material, and FIG. 4B enlarges one of the 8-chain models g constituting the network structure h. Showed. The network structure h in this example is assumed to have k 8-chain models g coupled in the width direction, the height direction, and the depth direction.

Now, when the total number of junction points b included in the mesh structure h is represented by the symbol m as “entanglement number”, the entanglement number m can be represented by Expression (12). Similarly, when the number of molecular chains c contained in the network structure h (that is, the number of molecular chains contained in the unit volume of the matrix model 3) is n, this n can be expressed by the formula (13). it can.
m = (k + 1) ³ + k ³ Formula (12)
n = 8k ³ (13)

Here, if k is a sufficiently large number, the above equations can be expressed by the following equations (14) and (15), respectively, except for the third-order term of k. The number m can be expressed by equation (16) using n.
m = 2k ³ Formula (14)
n = 8k ³ (15)
m = n / 4 Formula (16)

Further, assuming that the total number N _A of molecular chain segments contained in the matrix model 3 does not change even when the matrix model 3 is deformed, equations (17) to (18) are established.
N _A = n · N (17)
_{N = N A / n = N} A / 4m ... formula (18)

  In order to express the energy loss of the matrix model 3 in the simulation, the inventors have an idea that the entanglement number m of the molecular chain c of the viscoelastic material changes in the load application process and the subsequent strain recovery process. Tried. That is, as shown in FIG. 5A, for example, when tensile stress in the direction of the arrow acts on the molecular chains c1 to c4 joined at one joining point b, each molecular chain c1 to c4 expands, and the joining point b. Was considered to be damaged by large strain.

  As a result, as shown in FIG. 5B, the two molecular chains c1 and c2 that have been two so far are considered to behave as if they were one long molecular chain c5. The same applies to the molecular chains c3 and c4. Such a phenomenon is considered to occur sequentially as the load deformation of the rubber material proceeds.

The breakage of the junction point b as described above is nothing but a decrease in the number of entanglements m in the matrix model 3. Since the matrix model 3 itself has no material in and out, assuming that the total number N _A of the segments of the molecular chain c contained therein does not change, as the load deformation of the matrix model 3 proceeds, one molecular chain c It is clear from equation (18) that the average number N of included segments increases. That is, the average segment number N is not constant, and it is considered appropriate to use a variable parameter that is different between load deformation and unload deformation. Thereby, the energy loss when the matrix model 3 is deformed can be reproduced. This will be described in more detail later.

In order to more preferably reproduce such a situation on a computer, it is particularly preferable that the average number of segments N is increased according to a parameter relating to the strain at the time of load deformation. The parameter relating to the strain is not particularly limited, and examples thereof include a strain amount, a strain rate, or a first-order invariant I ₁ of strain. In the present embodiment, the average segment number N is a function of a parameter λc that is a square root of the first-order invariant I ₁ of strain in each element of the matrix model 3 as shown in the following equation (19). It shows what becomes.

Equation (19) is an example determined by various experiments, and A to E are constants and can be determined from actual measurement results such as a simple uniaxial tensile test of a rubber specimen. it can. In this example, the above constants are set as follows.
A = + 2.9493
B = −5.8029
C = + 5.5220
D = -1.3582
E = + 0.1325

  FIG. 6 shows the relationship between the average number of segments N and the parameter λc during load deformation of each element of the matrix model 3. As λc, which is a parameter related to strain, increases, the average segment number N increases smoothly. In this example, the upper limit of the parameter λc is 2.5. In the deformation simulation of the rubber material model 2 to be described later, the parameter λc is always calculated for each element of the matrix model 3 at the time of load deformation. The calculated λc is substituted into equation (19). Thereby, the average number of segments N in the strain state of the element can be calculated.

On the other hand, at the time of unloading deformation of the matrix model 3, the average number of segments N is a constant value. As a method for determining the average segment number N, for example, there is the following method. In the viscoelastic material to be analyzed, when there is one stress-strain curve, first, n and N are determined so as to match the unloading curve (that is, N _A = n · N is determined). Then, when the load, because the total number of segments N _A unloading during both molecular chain is identical, to match the load of the curve to determine the average number of segments N in each strain (where N is changed.) . Then, parameters A to E in Expression (19) are determined so as to match the determined average segment N at the time of loading. In this embodiment, N = 6.6 is used, and N at the end of load is set to be N at unloading.

  In the present embodiment, the filler model 4 is a model of carbon black as a filler. However, the filler is not limited to carbon black, and may be silica, for example. In this example, the physical shape of the filler model 4 is determined based on a shape obtained by imaging the shape of carbon black filled in actual rubber with an electron microscope. Specifically, the shape (minimum unit) of the carbon black 6 is, as schematically shown in FIG. 7, spherical primary particles 7 made of carbon atoms and having a diameter of about several tens of nm are irregularly bonded three-dimensionally. Has a tufted structure.

  In addition, since carbon black has a hardness (longitudinal elastic modulus) several hundred times that of a viscoelastic material such as rubber, the filler model 4 is handled as an elastic body instead of a viscoelastic body in this embodiment. Accordingly, the filler model 4 is given a longitudinal elastic modulus as a material characteristic, and stress and strain are proportional in deformation calculation. The amount of the filler model 4 is appropriately determined in consideration of the amount added to rubber.

  The interface model 5 is set around the filler model 4. As a physical structure, it has not been confirmed that such a special layer is formed at the interface between the filler and the rubber matrix. However, as described above, various phenomena occur at the interface between the filler and the matrix rubber. Especially, slipping or friction phenomenon at the interface causes a relatively large energy loss.

  The interface model 5 of the present embodiment continuously surrounds the filler model 4 and is set with a small thickness, and viscoelastic characteristics different from the matrix model 3 are defined. This is useful for enabling a large energy loss to be reproduced at the interface in the rubber material model 2. The interface model 5 is not necessarily limited to a form that continuously surrounds the filler model 4, but it is desirable to surround most of the interface model 5. The thickness t of the interface model 5 is not particularly limited, but if it is too large, the energy loss tends to be excessively expressed, and conversely if it is too small, it is difficult to reproduce the energy loss at the interface. As a result of various experiments, the thickness t is desirably 1 to 20 nm, and more preferably 5 to 10 nm, for example.

  The interface model 5 is handled as a viscoelastic material. Therefore, the relationship between stress and strain is defined based on the above equation (3) as in the matrix model 3. The interface model 5 of the present embodiment defines viscoelastic properties that are softer than the matrix model 3. Specifically, the slope of the elastic component (corresponding to the longitudinal elastic modulus of the elastic body) in the stress-strain (or elongation) curve is made smaller than that of the matrix model 3. Further, the interface model 5 of the present embodiment defines viscoelastic characteristics having a larger hysteresis loss (energy loss generated per strain cycle) than the matrix model 3.

  Next, in the simulation method of the present embodiment, a deformation simulation is performed using the set rubber material model 2 (step S3). A specific processing procedure of the deformation simulation is shown in FIG. In the deformation simulation, first, data is input to the computer apparatus 1 (step S31). The input data includes information such as the positions of nodes and material properties defined for each element.

  The computer apparatus 1 creates a stiffness matrix for each element based on the input data (step S32), and then assembles a stiffness matrix for the entire structure (step S33). Displacement of known nodes and nodal forces are introduced into the stiffness matrix of the entire structure (step S34), and the stiffness equation is analyzed. Then, unknown node displacement is determined (step S35), and physical quantities such as strain, stress and principal stress of each element are calculated and output (steps S36 to 37). In step S38, it is determined whether or not to end the calculation. If negative, step S32 and subsequent steps are repeated.

  The simulation can be performed using, for example, engineering analysis application software using the finite element method (for example, LS-DYNA developed and improved by Livermore Software Technology, USA).

This simulation illustrates an embodiment performed based on a homogenization method (asymptotic expansion homogenization method). As shown in FIG. 9, the homogenization method includes x _I representing the entire rubber material M periodically having the microscopic structure (unit cell) shown in FIG. 3, and y representing the microscopic structure. two independent variables and _I is used. By asymptotically expanding each independent variable in different scale fields, the microscopic scale and the macroscopic scale, the average mechanical response of the entire rubber material reflecting the model structure of the microscopic structure shown in FIG. Can be sought. In other words, if the analysis target area is composed of repetitions of an arbitrary microscopic structure, and the repetition degree is so dense that the area cannot be discretized directly by the finite element method, the analysis target is replaced with a homogeneous equivalent model. By analyzing the whole and returning the analysis result to the microscopic structure at an arbitrary point, the deformation of the microscopic structure itself can be obtained approximately. The asymptotic expansion homogenization method is described in detail, for example, in the following document.
Higa, Y. And Tomita, Y ,, Computational Prediction of Mechanical Properties of Nickel-based superalloy with gamma Prime Phase Precipitates, Proceedings of ICM8 (Victoria, BC, Canada), Advance Materials and Modeling of Mechanical Behavior, (Edited by Ellyin, F, and Proven, JW), III (1999), 1061-1066, Fleming Printing Ltd.
Yoshikazu Higa, Yoshihiro Hamada, Modeling and Simulation of Deformation Behavior by Homogenization Method of Particle Reinforced Composites, Transactions of the Japan Society of Mechanical Engineers, A66 (2000), 1441-1446.
Specifically, in addition to the equation (3), a macroscopic equilibrium equation of the following equation (20) and a characteristic displacement function (Y-periodic) of the equation (21) are used.

Further, in the present embodiment, the constants of Expression (3) are set as follows.
C ^R = 0.268
N = 6.6
T = 296
k _B = 1.38066 × 10 ⁻²⁹
n = C ^R / K _B /T=6.558×10 ²⁵
N _A = n · N = 4.328 × 10 ²⁶
Volume content of filler model 30%
Longitudinal elastic modulus E of filler model: 100 MPa
Poisson's ratio ν of filler model: 0.3

In the deformation simulation, a rectangular analysis region of 2 mm × 2 mm is set as the macroscopic model M, and an average strain rate 1 in the x2 direction of FIG. 9 is generated in order to generate uniform uniaxial tensile deformation in the macroscopic model M. 0.0 × 10 ⁻⁵ / s is added and the strain is gradually increased from zero to 2.5 in steps of 0.01, and the stress acting on the rubber material model 2 is calculated for each strain. On the contrary, after the strain reached 2.5, the strain was gradually reduced to zero at the same strain rate as described above in increments of 0.01. In each strain state, the average number of segments N is calculated, and this value is substituted into equation (3) for sequential calculation. As the rubber material model, a three-dimensional 8-chain model of Arruda et al. Is used so as not to change in the thickness direction (Z-axis direction in FIG. 3). The average number of segments N of the matrix model 3 and the interface model 5 was set as follows.

<Matrix model>
・ Average number of segments N during load deformation
N = -3.2368 + 20.6175 λc-21.8168 λc ² + 10.8227λc ³ -1.9003 λc ⁴
・ Average number of segments N during unloading deformation (constant)
N = 6.6
・ Total number of molecular chain segments N _A (constant)
N _A = 4.3281 × 10 ²⁶

<Interface model>
・ Average number of segments N during load deformation
N = -5.9286 + 20.6175 λc-21.8168 λc ² + 10.8227λc ³ -1.9003 λc ⁴
・ Average number of segments N during unloading deformation (constant)
N = 3.91
・ Total number of molecular chain segments N _A (constant)
N _A = 3.203 × 10 ²⁵

  When the deformation calculation is performed, a necessary physical quantity can be acquired from the result (step S4). FIG. 10 shows the results of the deformation simulation performed independently for each of the matrix model 3, the filler model 4, and the interface model 5. The filler model 4 shows the highest elasticity and no energy loss occurs. The interface model 5 shows viscoelastic characteristics that cause a larger strain than the matrix model 3 even at the same stress, and the energy loss (the loop area of the curve) is also large.

  A curve La in FIG. 11 shows the relationship between the true stress and strain in the entire rubber material model in which the above models are incorporated as the microscopic structure (cell unit) in FIG. At the time of load deformation, a non-linear first curve La1 was obtained. Further, at the time of unloading deformation, a second curve La2 different from the first curve La1 was obtained. The second curve La2 was softer than the first curve La1 (low elasticity), and a hysteresis loop could be reproduced. By calculating the closed area of this loop, the energy loss in one deformation cycle can be calculated.

  By the way, when the same deformation simulation as Arruda et al. Was performed with the average number of segments N per molecular chain being constant, the result of not being able to express energy loss through the same curve during load deformation and unload deformation. It becomes. In the above embodiment, the average segment number N is a function of the parameter λc. However, a strain rate or a strain amount can be used instead of λc. In this case, similarly to the equation (19), the energy loss can be expressed by changing the coefficient between the load deformation and the unload deformation.

  The shape of each of the curves La1 and La2 can be variously set by appropriately setting the coefficients A to E and changing the function for determining the average number of segments N per molecular chain in the equation (19). Therefore, for example, energy loss can be examined in detail for each material by setting various coefficients A to E according to the rubber material to be analyzed. This is very useful for improving the performance of tires and golf balls using viscoelastic materials as the main part. Further, when the stress-strain curve of the material to be simulated is known, by adjusting the coefficients A to E and the like accordingly, the viscoelastic material representing the same stress-strain relationship as the actual viscoelastic material can be obtained. Simulation can be performed easily.

  Further, FIG. 11 shows a result obtained by performing the same experiment on a model in which the same material characteristics as the matrix model 3 are given to the interface model 5 (that is, a model not considering the interface) as a curve Lb. Yes. In the rubber material model 2, the curve Lb has no soft region at the interface where a large strain occurs, so that the slope of the stress-strain curve rises more than the curve La. Moreover, since a large energy loss is unlikely to occur at the interface as in the interface model 5, the energy loss of the entire model is also small.

  Further, in FIG. 11, a result of performing a simulation by giving the interface model 5 a material characteristic opposite to that of the curve La is shown as a curve Lc. That is, the rubber material model 2 showing the curve Lc is defined in terms of viscoelasticity so that the interface model 5 exhibits higher elasticity than the matrix model 3 as shown in FIG. As a result, it can be confirmed that the viscoelastic property of the entire system of the rubber material model 2 has a much higher gradient than the curve Lb and is highly elastic. In this embodiment, the average segment number N of each model is set as follows.

<Matrix model>
・ Average number of segments N during load deformation
N = -3.2368 + 20.6175 λc-21.8168 λc ² + 10.8227λc ³ -1.9003 λc ⁴
・ Average number of segments N during unloading deformation (constant)
N = 6.6
・ Total number of molecular chain segments N _A (constant)
N _A = 4.3281 × 10 ²⁶

<Interface model>
・ Average number of segments N during load deformation
N = -5.4800 + 20.6175 λc-21.8168 λc ² + 10.8227λc ³ -1.9003 λc ⁴
・ Average number of segments N during unloading deformation (constant)
N = 4.36
・ Total number of molecular chain segments N _A (constant)
N _A = 8.569 × 10 ²⁶

  FIG. 13 intermittently visualizes the process of deformation to recovery in one microscopic structure (unit cell) in the uniaxial tensile deformation simulation of the rubber material model 2 (curve La). . FIGS. 13A to 13E show load deformation, and FIGS. 13F to 13J show unload deformation. Moreover, the place where the color is changing to white indicates a region with a large distortion. This result accurately reproduces that a large strain is concentrated between the interface of the filler model 4 and between the filler models 4 and 4. In particular, it can be seen that a large strain occurs in a portion where the distance between the filler models 4 and 4 is small.

  FIG. 14 shows the strain distribution in the tensile direction of each element at the maximum strain, (A) shows the curve Lb in FIG. 11 not considering the interface, and (B) shows the curve La in consideration of the interface. Is. The thinner the color, the greater the distortion. In the case of (A) in which the interface is not taken into consideration, the generation of strain is broadly and gently generated as a whole, whereas in the case of (B) in which the interface is taken into consideration, around the filler model 4 It is well reproduced that large strains are concentrated.

  In FIG. 15, the energy loss of one cycle of strain is calculated for each element, and the magnitude is shown by color. The lighter the color, the greater the energy loss. Further, the shape of the model is represented by the maximum deformed shape in FIG. 14, (A) is the curve Lb in FIG. 11, and (B) is the curve La. In the case of (B) considering the interface, it can be confirmed that a large energy loss occurs at the interface of the filler model 4.

  Such a simulation can accurately evaluate the viscoelastic characteristics including energy loss for rubber materials in which the blending ratio of filler to the rubber material and the type of filler are variously changed.

It is a perspective view which shows an example of the computer apparatus used by this embodiment. It is a flowchart which shows the process sequence of this embodiment. It is a diagram showing one embodiment of a rubber material model (microscopic structure). (A) is a perspective view which shows the network structure of a viscoelastic material, (B) is a perspective view which shows an example of an 8-chain model. (A), (B) is a diagram explaining the fracture | rupture of the junction of a molecular chain. It is a graph which shows the relationship between parameter (lambda) c and the average number of segments N per molecular chain. It is a diagram which shows the shape of carbon black. It is a flowchart which shows the procedure of a deformation | transformation simulation. The relationship between the microscopic structure explaining the homogenization method and the entire structure is shown. The individual stress-strain curves of the matrix model, filler model and interface model are shown. It is a graph which shows the relationship between true stress-strain as a simulation result of a rubber material model (whole structure). The stress-strain curve which shows the other example of a matrix model and an interface model is shown. (A)-(J) are the diagrams which visualize and show the deformation process of a rubber material model. (A) is a model in which the interface layer is not considered, and (B) is a tensile strain distribution diagram of the model in which the interface layer is considered. (A) is a model in which the interface layer is not considered, and (B) is an energy loss distribution diagram of the model in which the interface layer is considered. (A) is a viscoelastic material, (B) is a diagram for explaining the structure of one molecular chain, (C) is an enlarged view of one molecular chain, and (D) is an enlarged view of a segment. As a simulation result by Arruda et al., A stress-strain curve is shown.

Explanation of symbols

1 Computer device 2 Rubber material model 3 Matrix model 4 Filler model 5 Interface model

Claims (5)

A rubber material simulation method for simulating deformation of a rubber material containing a filler,
Setting a rubber material model obtained by modeling the rubber material with an element capable of numerical analysis;
Performing deformation calculation by setting conditions in the rubber material model;
Obtaining a necessary physical quantity from the deformation calculation, and
The rubber material model includes a matrix model that models a rubber matrix, a filler model that models a filler, and an interface model that forms an interface between the matrix model and the filler model. Rubber material simulation method.   The rubber material simulation method according to claim 1, wherein the interface model defines viscoelastic characteristics different from the matrix model.   The rubber material simulation method according to claim 1, wherein the interface model defines viscoelastic properties that are softer than the matrix model.   The rubber material simulation method according to claim 1, wherein the interface model defines viscoelastic properties that are harder than the matrix model.   5. The rubber material simulation method according to claim 1, wherein the interface model defines viscoelastic characteristics having a hysteresis loss larger than that of the matrix model.